EP1038978A1 - Process and installation for manufacturing hot strip - Google Patents

Abstract

Hot rolled microalloyed steel strip production, uses inter-stand cooling to allow final rolling passes at a temperature below the recrystallization temperature. Production of hot rolled strip (W) of unalloyed or low alloy steel containing micro-alloying elements, from optionally reheated continuously cast slabs, plates or strip, comprises: (a) feeding strip into the first stand (F1) of a tandem finishing line (FS) at ≥ 30 degrees C above the recrystallization end temperature (TR); (b) continuously rolling the strip in one or more passes in the austenite recrystallization region; (c) cooling the strip between adjacent stands (F1-F7) by cooling devices (K2-K7) to ≥ 20 degrees C below the recrystallization end temperature (TR) at a cooling rate of ≥ 10 degrees C/sec.; and (d) rolling the strip at below the recrystallization end temperature (TR) in several passes with a total deformation ( epsilon h) of ≥ 30%. An Independent claim is also included for a hot strip line for carrying out the above process.

Description

The invention relates to a method for producing a Hot strip based on an unalloyed or low alloy steel with additions of Continuous casting micro alloying elements in the form of reheated or straight from the pouring heat used slabs, thin slabs or cast tape is generated, the hot strip being one of several Rolling stands formed finished series passes. Methods of this type are used to make high-strength Manufacture hot strips of high toughness.

For example from the essay "Optimizing the Hot rolling conditions to improve and Uniformization of the material properties ", K. Kaup, W. Haumann, G. Gorges, W. Fabian, Stahl u. Iron 104 (1984), pp. 1017-1024, methods are known in which the hot strip is pre-rolled in the recrystallization area, then cooled and then at a temperature which is below the recrystallization temperature, is finished rolling. For this purpose it is necessary to guide the rolling process during roughing so that the Supporting surface before the last forming stitch of the Pre-rolling to temperatures just above the Recrystallization temperature has cooled. This can lead to one can be achieved by an additional Cooling section is provided in the area of the roughing mill.

If the corresponding space is not available, the Rolling process for one sufficient for cooling Time can be delayed. This delay while which the supporting strip in the area between the roughing stand and the finished relay is moved back and forth ("commutes"), leads to an undesirable extension of the Production process. Can during a long commute it also becomes an undesirable one Austenite grain growth and excretions come through which the structural development after the last forming stitch in the roughing mill and during the subsequent finishing rolling is negatively influenced in the finished series. So can after finish rolling in hot strip austenite mixed grain structures be present that has a negative Influence on the structure development within the framework of the γ / α conversion Exercise on the exit roller table and in the coil.

The latter leads in particular to hot strip thicknesses of 8 mm and more to an undesirably inhomogeneous structure over the Belt cross-section, through which in particular the toughness is reduced to an undesirable extent. Especially this loss of toughness has an adverse effect microalloyed steel grades with high Toughness requirements, for example for oil or gas pipeline construction.

From the German patent application DE 197 25 434 A1 is a process for rolling hot strip continuously cast thin slabs in a so-called "Compact-Strip-Production (CSP)" line known. At Such CSP lines become continuous Pre-material after dividing into roll lengths over one Compensation furnace fed directly to the rolling mill. Here there is a peculiarity compared to conventional Production lines in that the thin slab with Casting structure is introduced into the finished series.

In the aforementioned publication, for producing a hot wide strip from a ferritic-pearlitic microalloyed structural steel with a microalloy with vanadium, niobium and / or titanium, it is proposed to change the casting structure of the material introduced into the finished series by setting defined temperature or shape change conditions during the first forming . The temperature of the material during the first forming is above the recrystallization stop temperature. The change mentioned is to be carried out in such a way that a complete recrystallization of the casting structure takes place before or after the second forming step, during or after the first forming. The hot strip is then to be rolled at a temperature below the recrystallization stop temperature. The deformation achieved should not be less than 30%. In addition, a final rolling temperature close to the Ar ₃ temperature is to be achieved.

To ensure that the recrystallization before second reshaping is completed in furthermore proposes the aforementioned publication, at least the second mill stand of the finishing line open or use as a driver if necessary. To this Way, the hot strip formed in the first stage enough time to cool down before it is the second Forming is subjected.

Such a procedure can also be used for one CSP system is divided into two defined sections Rolling, namely rolling in the recrystallization area of the austenite and the subsequent rolling in the area below the recrystallization stop temperature, carry out. This procedure is disadvantageous however, that the rolling performance is at least one of those in the Finishing scale available roll stands not can be used. This leads to a significant one Limitation of the maximum achievable in finish rolling Forming degrees and, associated with it, to a considerable limitation of the variety of products that can be produced with such a method.

The object of the invention is a method of the type specified at the beginning and one for implementation such a method particularly suitable device to create which enable a high strength Hot strip with excellent toughness inexpensive to manufacture.

• Einleiten des Warmbandes in das erste Walzgerüst der Fertigstaffel mit einer Temperatur, welche um mindestens 30 °C über der Rekristallisationsstop-Temperatur liegt,
• kontinuierlich erfolgendes Walzen des Warmbandes in einem oder mehreren Stichen im Rekristallisationsbereich des Austenits,
• Abkühlen des Warmbandes zwischen zwei Walzgerüsten mittels einer Kühleinrichtung auf eine Temperatur, welche mindestens 20 °C unterhalb der Rekristallisationsstop-Temperatur liegt, mit einer Abkühlgeschwindigkeit, welche mindestens 10 °C/s beträgt,
• Walzen des unterhalb der Rekristallisationsstop-Temperatur abgekühlten Warmbandes in mehreren Stichen bei einem Gesamtumformgrad von mindestens 30 % im Temperaturbereich unterhalb der Rekristallisationsstop-Temperatur.

This object is achieved with respect to the method in that a method for producing a hot strip, which is produced on the basis of an unalloyed or low-alloy steel with additions of micro-alloy elements from continuous casting in the form of slabs, thin slabs or strip, the hot strip being one of several roll stands completed pre-season, includes the following steps:

• Introducing the hot strip into the first mill stand of the finished batch at a temperature which is at least 30 ° C. above the recrystallization stop temperature,
• continuous rolling of the hot strip in one or more passes in the recrystallization area of the austenite,
• Cooling the hot strip between two roll stands by means of a cooling device to a temperature which is at least 20 ° C. below the recrystallization stop temperature, with a cooling rate which is at least 10 ° C./s,
• Rolling the hot strip cooled below the recrystallization stop temperature in several passes with a total degree of deformation of at least 30% in the temperature range below the recrystallization stop temperature.

Can be particularly advantageous with the invention Process produce a hot strip, which from a Steel is produced which in mass% C: ≤ 0.18%, Si: ≤ 1.5 %, Mn: ≤ 2.5%, P: 0.005 - 0.1%, S: ≤ 0.03%, N: ≤ 0.02 %, Cr: ≤ 0.5%, Cu: ≤ 0.5%, Ni: ≤ 0.5%, No: ≤ 0.5%, Al ≤ 2%, up to a total of 0.3% of one or more of the Elements B, Nb, Ti, V, Zr and the balance iron and contains inevitable impurities.

According to the invention, the rolling stock when it is in the Finished season is initiated, a temperature which safely above the recrystallization stop temperature lies. This inlet temperature is set so that at least the first forming of the hot strip in the Finished scale in the recrystallization area of austenite is carried out. Through this in Recrystallization area of the austenite rolls grain refinement is achieved.

After the first, or if necessary, another Forming in this temperature range becomes the hot strip between two of the mill stands of the finished series with one suitable cooling device so strong and fast cooled that its temperature when entering the following mill stand below the recrystallization stop temperature lies.

In this context, it can be beneficial if that Hot strip before it is on between the two rolling stands those below the recrystallization stop temperature lying temperature is cooled, at least once is cooled between previously passed mill stands, without increasing the recrystallization stop temperature fall below. This is particularly useful if the hot strip with a high temperature in the Finished relay arrives. By the decisive Cooling step below the recrystallization stop temperature upstream cooling you "feel" the Temperature, from which the Rolled material up to at least 20 ° C below the Recrystallization stop temperature is cooled. It remains essential that this is decisive Cooling below the recrystallization stop temperature defined between two rolling stands.

According to the invention, the hot rolling of the hot strip should take place in the austenite area. The final rolling temperature of the hot strip should therefore be greater than Ar ₃ + 30 ° C when leaving the finishing train.

The method according to the invention makes it possible to the method known from DE 197 25 434 A1, in one process carried out continuously to produce particularly good material properties. These excellent material qualities can be seen in Procedure according to the invention also for hot strips achieve that from steels with diminished or even not present levels of expensive alloy and Microalloying elements such as Ti, Nb, V have been created are. Thus, by using the invention existing steel concepts with new steel qualities higher strength and excellent toughness become. In the case of known steel grades, alloy contents be saved without becoming a negative Influencing the property spectrum comes.

Costly cooling sections with high space requirements or additional process times required for cooling are not required in the invention. Likewise, the Rolling capacity of all available in the finishing line standing mill stands are fully used, so that with the Invention an unlimited range of products can be manufactured.

The method according to the invention is self-evident not on the use of thin slabs or pre-rolled material is limited as the starting material, which is processed directly from the pouring heat. As well can the invention within the conventional Hot strip rolling are used in the Continuous cast slabs are reheated before entering the Rolling mill to be introduced.

With the method according to the invention Produce hot strips, which have a cross-section have a very fine-grained and homogeneous structure. The with conventional thermo-mechanical hot rolling usually fine-grained Structural structure is the procedure according to the invention refined further. It has been found that a conventionally thermo-mechanically rolled, 12.7 mm thick Hot strip with a set according to API X65 Microstructure with a pearlite-ferrite structure has an average ferrite grain diameter of 5 - 7.5 µm. A comparable hot strip shows after it has undergone a method according to the invention average ferrite grain diameter of 3.5 to 4.5 microns. Ferrite grain inhomogeneities in the strip core become avoided. The same applies to the excretion state, which has a finer dispersion and one Amount of precipitation hardening leads, which over the to be expected for conventionally rolled hot strips goes out.

It was also found that the toughness of the hot strips produced according to the invention despite improved yield strength and higher strip thickness improved is. The transition temperature for 80% matt break at BDWT test was up to 25 ° C lower temperatures postponed.

According to the inventive method, the Rolling temperatures taking into account the Recrystallization stop temperature unerringly and very can be set precisely. This enables the rolling in the recrystallization area just above the Carry out recrystallization stop temperature. So can the austenite grain refinement can be optimally used. The subsequent forming below the The recrystallization stop temperature then becomes Solidification of the fine-grained austenite grain structure used. This fine-grained and solidified Austenite structure leads to an optimal, very fine Structural structure after the γ / α conversion.

Furthermore, in the invention deformation-induced excretion processes on the only a short time consuming deformation in the last stands of the finishing mill. The Proportion of the excreted micro-alloy contents significantly reduced due to this short period of time. At the same time, the elimination potential for the Precipitation hardening of the structure after the γ / α conversion better used.

Another advantage of the procedure according to the invention is that the surface condition of the hot strip is positively influenced. Through targeted cooling between the mill stands the scale formation is almost completely suppressed so that little material loss arise and the hot strip in the delivery condition with a small scale layer of less than 10 µm is occupied. On the one hand, this has advantages in direct use well adhering because thin scale, as expected for example in the manufacture of gas bottles, which painted without descaling after forming become. On the other hand, in cases where the Hot strip is descaled before it is processed, the time required for pickling, for example, is reduced and the capacity of the stain can be increased.

With regard to the hot strip line for carrying out the This accomplishes the above-mentioned task solved that at least in one of the two Rolling frames of the finishing line free spaces a cooling device is arranged. This in addition to the usual cooling of the roll stands Cooling device is able to remove the hot strip during the Transition from one to the next mill stand so strong cool that the recrystallization area of the Austenite is completely left after cooling and the subsequent rolling at temperatures below the Recrystallization stop temperature is carried out.

The cooling device advantageously brings at least a high-pressure water jet whose volume flow is adjustable. With such a design Cooling device can easily reduce the cooling capacity be adapted to the respective requirements. The latter applies in particular if the Cooling device comprises several nozzles, which individually or coolant can be applied in groups. It is also favorable, if not only between one of the a respective cooling device is provided, but if in several of the between two existing stands one each such device is arranged. This gives the Possibility to change the hot strip to a Temperature below the recrystallization stop temperature targeted at that for the respective rolling process optimal position with regard to the desired result perform.

Further advantageous embodiments of the invention are specified in the dependent claims.

Fig. 1

die Fertigstaffel und den Auslaufrollgang einer Walzstraße in seitlicher Ansicht;

Fig. 2

den über die Zeit aufgetragenen Temperaturverlauf während des Walzens in der Fertigstaffel der Walzstraße.

The invention is explained in more detail below using an exemplary embodiment. In a schematic representation:

Fig. 1

the finishing scale and the run-out roller table of a rolling mill in a side view;

Fig. 2

the temperature profile plotted over time during rolling in the finishing line of the rolling mill.

In the exemplary embodiment explained here, the Finished relay FS from seven roll stands F1, F2, F3, F4, F5, F6, F7 formed by a hot strip W in the direction of conveyance E one after the other. It it goes without saying that the finished relay FS ever according to their design and performance with a fewer or a larger number of roll stands can be equipped.

Upstream of the first roll stand F1 in the conveying direction F. is a first cooling device K1. This cooling device K1 has nozzles, not shown, over which water is blasted under high pressure on the hot strip W, before it enters the first mill stand F1.

In each of the mill stands F1, F2; F2, F3; F3, F4; F5, F6; F6, F7 each of the remaining rooms R. one cooling device each K2, K3, K4, K5, K6, K7 arranged. The cooling devices K2 - K7 have also nozzles, which via supply lines L are connected to a control device S. About the Control device S are the nozzles of Cooling devices K2 - K7 optionally with high pressure standing cooling water. The work here Cooling devices K2 - K7 additionally and independently of the cooling systems with which the respective rolling stands F1 - F7 are equipped as standard.

In the area of the run-out roller table A is at a short distance to the last rolling stand F7 of the FS 1 finishing line conventionally designed cooling device K8, in the manner of a laminar cooling section or a accelerated cooling enabling compact cooling section Cooling water can be applied to the hot strip W. At the The end of the run-out roller table A is finally a reel device H, in which the hot strip W to Coils C can be wound.

For example, made from conventional continuous casting, then cooled, reheated and pre-rolled hot strip W is cooled in the first cooling device K1 by means of water applied under high pressure to a temperature which is in the range of a little more than 30 ° C above the recrystallization stop temperature T _{REK STOP} des Steel lies from which the hot strip W has been produced. Alternatively, a thin slab inserted and pre-rolled directly from the casting heat or a strip produced by casting close to the final dimensions can be introduced into the finished batch. If necessary, the slab or the strip is cooled by the cooling device K1 to the required temperature T ₁ above the recrystallization stop temperature.

The hot strip W cooled in this way is subjected to a first forming in the first roll stand F1. Since the temperature of the hot strip W is above the recrystallization stop temperature T _{REK STOP} during this first forming, this forming takes place within the recrystallization area of the austenite.

A formal connection for determining the Recrystallization stop temperature depending certain alloying elements is, for example, from the Article "Determination of Recrystallization Stop Temperature from Rolling Mill Logs and Comparison with Laboratory Simulation Results ", T.M. Maccagno et al., ISIJ International, Vol. 34 (1994) No. 11, pp. 917-922, known.

After the first forming process, the hot strip W is cooled, for example, by the cooling water, which is applied by the cooling device K2 between the first and the second roll stands F1, F2 under high pressure, at a cooling rate of more than 10 ° C./s to a temperature which is at least 20 ° C is lower than the recrystallization stop temperature T _REK-STOP . The hot strip W cooled in this way is finish-rolled in the roll stands F2 to F7 in the non-recrystallized area of the austenite, an overall degree of deformation ε _{h being achieved} in these roll stands F1-F7, which is more than 30%. The further cooling devices K3-K7 arranged between the subsequent rolling stands F2-F7 remain inoperative in this case.

If, on the other hand, a greater degree of deformation is required when rolling in recrystallized austenite, the temperature T ₁ with which the hot strip W enters the finishing season FS can be set by a corresponding cooling capacity of the cooling device K1 so that the hot strip W, with a temperature above the recrystallization stop temperature T _{REK STOP} also enters the second roll stand F2 in order to be rolled there in the recrystallization area of the austenite as well. In this case, the hot strip W can then be cooled by the third cooling device K3 at cooling speeds of more than 10 ° C / s to a temperature T _{2 which} is at least 20 ° C below the recrystallization stop temperature T _{REK STOP} and in the following roll stands F3 to F7 in the non-recrystallized austenite area with a total degree of deformation of at least 30%. The cooling device K2 between the roll stands F1, F2 can be used to lower the temperature of the hot strip W before it enters the second roll stand F2, but without falling below the recrystallization stop temperature T _{REK STOP} (FIG. 2).

By in the space R between each of the pairs of stands F2, F3; F3, F4; F4, F5; F5, F6; F6, F7 a cooling device K2 - K7 is arranged, the decisive step of cooling below the recrystallization stop temperature T _{REK STOP} can thus be carried out at the point of the finished scale FS that is most favorable for the properties of the processed hot strip W. In this case, the cooling devices which have passed through this crucial cooling can be used to cool the hot strip W without falling below the recrystallization stop temperature T _{REK STOP} . In this way, among other things, the need for cooling power in the decisive cooling can be reduced from a temperature above the recrystallization stop temperature T _{REK STOP} to a temperature below the recrystallization stop temperature T _{REK STOP} .

The hot strip W exiting the finishing season FS with a temperature T ₃ above the A _r3 temperature enters the fourth cooling device K4 at the latest after 10, but preferably after only 2 seconds. In it, it is cooled at a cooling rate of more than 20 ° C./s to a coiling temperature of not more than 650 ° C., preferably not more than 550 ° C. The hot strip W cooled in this way is finally coiled on the reel device H to form a coil C.

The hot strip W produced in this way becomes more advantageous Way to a cold strip with a thickness of less than 5 mm cold rolled, the during the cold rolling achieved total degree of deformation at least 55% should. In this context, it is also advantageous when the cold strip is annealed to recrystallize. Here Depending on the desired property of the End product in a hood or a continuous furnace be performed. It is also possible to do this to provide annealed cold rolled strip with corrosion protection, that in the form of hot dip galvanizing or electrolytically applied coating is formed.

In Table 1, for three made of a steel with mass% 0.06% C, 0.28% Si, 1.07% Mn, 0.019% P, 0.001% S, 0.03% Al, 0.11% Cu, 0.05% Ni, 0.007% N, 0.057% Nb, 0.056% V, remainder iron and unavoidable impurities, hot strip samples P _K1 , P _K2 , P _K3 produced in a conventional procedure, the respective thickness D in mm, the finish rolling temperature ET in ° C, the reel temperature HT in ° C, the yield strength R _e in N / mm ² , the tensile strength R _m in N / mm ² , the elongation at break A in%, the results of the BDWT test BDWT 0 ° C in% or BDWT 85% in ° C and the respective mean ferrite grain diameter FK _m in µm. D ET HT R _e R _m A BDWT 0 ° C BDWT 85% FK _m P _K1 12.7 870 620 494 563 48 96 -10 5.7 P _K2 12.7 865 590 496 609 44 69 10th 7.2 P _K3 12.7 865 620 470 581 44 87 5 7.0

As far as determined, Table 2 summarizes the same information for six hot strip samples P _E1 , P _E2 , P _E3 , P _E4 , P _E5 , P _E6 produced from the same steel in accordance with the invention.

A comparison of the material properties of the hot strip samples P _K1 , P _K2 , P _K3 produced by the conventional method with the properties of the hot strip samples P _E1 , P _E2 , P _E3 , P _E4 , P _E5 , P _E6 clearly shows that the hot strips produced according to the invention have considerably improved strength properties with a greater thickness, a significantly improved fraction of matt breakage and a much finer grain size. D ET HT R _e R _m A BDWT 0 ° C BDWT 85% FK _m P _E1 14.5 845 600 540 592 41 100 -15 3.9 P _E2 14.5 845 600 515 580 39 100 -15 4.3 P _E3 14.5 835 630 526 597 43 100 -30 3.5 P _E4 14.5 830 600 505 578 39 4.4 P _E5 14.5 830 600 504 575 30th 98 -5 4.3 P _E6 14.5 820 600 540 622 37 94 -5 4.2

REFERENCES

A

Outlet roller table

C.

Coil

ε _H

Total degree of deformation after the Cooling below the Stop recrystallization temperature

ET

Final temperature of the hot strip at Leaving the finished relay FS

F

Direction of conveyance

FS

Finished relay

F1, F2, F3, F4, F5, F6, F7

Mill stands

H

Decoiler

HT

Reel temperature

K1 - K8

Cooling devices

L

Supply lines

R

Space between two Roll stands

S

Control device

T ₁

Temperature of the in Finishing season entering Hot strip W

T _{REK STOP}

Stop recrystallization temperature

T ₂

Temperature below T _{REK STOP}

W

Hot strip

Claims (16)

Process for producing a hot strip (W), which is produced on the basis of an unalloyed or low-alloy steel with additions of micro-alloy elements from continuous casting in the form of re-heated slabs, thin slabs or cast strip, which is inserted directly from the casting heat, the hot strip (W) being a finished batch (FS) formed from several rolling stands (F1 - F7), comprising the following steps: Introducing the hot strip (W) into the first rolling stand (F1) of the finishing assembly (FS) at a temperature (T ₁ ) which is at least 30 ° C. above the recrystallization stop temperature (T _REK-STOP ), continuous rolling of the hot strip (W) in one or more passes in the recrystallization area of the austenite, Cooling the hot strip (W) between two rolling stands (F1, F2; F2, F3; F3, F4; F4, F5; F5, F6; F6, F7) by means of a cooling device (K2 - K7) to a temperature (T ₂ ), which is at least 20 ° C below the recrystallization stop temperature (T _REK-STOP ), with a cooling rate which is at least 10 ° C / s, Rolling the hot strip (W) cooled below the recrystallization stop temperature (T _REK-STOP ) in several passes with a total degree of deformation (ε _h ) of at least 30% in the temperature range below the recrystallization stop temperature (T _REK-STOP ). A method according to claim 1, characterized in that the steel in mass% - C: ≤ 0.18% - Si: ≤ 1.5% - Mn: ≤ 2.5% - P: 0.005 - 0.1% - S: ≤ 0.03% - N: ≤ 0.02% - Cr: ≤ 0.5% - Cu: ≤ 0.5% - Ni: ≤ 0.5% - Mon: ≤ 0.5% - Al: ≤ 2% - up to a total of 0.3% of one or more of the elements B, Nb, Ti, V, Zr and as - rest of iron and unavoidable impurities contains. Method according to one of the preceding claims, characterized in that the final rolling temperature (ET) of the hot strip (W) is greater than Ar ₃ + 30 ° C when leaving the finishing season (FS). Method according to one of the preceding claims, characterized in that the hot strip (W) before it between the two roll stands (F1, F2; F2, F3; F3, F4; F4, F5; F5, F6; F6, F7) on the below the Rekristallisationsstop temperature (T _REK-STOP) lying temperature (T ₂₎ is cooled, at least (F1 - F7) once between previously passed through roll stands is cooled, without falling below the Rekristallisationsstop temperature (T _REK-STOP). Method according to one of the preceding claims, characterized in that the hot strip (W) after leaving the finished season (FS) at the latest after 10 seconds with a cooling rate of more than 20 ° C / s to a coiling temperature (HT) of not more than 650 ° C cooled and then coiled. A method according to claim 5, characterized in that the cooling of the hot strip (W) begins at the latest 2 seconds after leaving the finishing line (FS). Method according to one of claims 5 or 6, characterized in that the reel temperature (HT) is not more than 550 ° C. Method according to one of the preceding claims, characterized in that the hot strip (W) is hot-dip galvanized at temperatures of not more than 650 ° C. Method according to one of the preceding claims, characterized in that the hot strip (W) is cold-rolled into a cold strip with a thickness of less than 5 mm and that the overall degree of deformation achieved during cold rolling is at least 55%. A method according to claim 9, characterized in that the cold strip is annealed to recrystallize. Method according to claim 10, characterized in that the cold strip is hot-dip galvanized. Method according to one of claims 10 or 11, characterized in that the cold strip is electrolytically provided with a corrosion protection. Method according to one of the preceding claims, characterized in that the thickness of the hot strip (W) is at least 8 mm. Hot strip line for carrying out the method according to one of the preceding claims, with a finishing mill (FS) formed from a plurality of roll stands (F1 - F7), characterized in that at least one of the two roll stands (F1, F2; F2, F3; F3, F4; F4, F5; F5, F6; F6, F7) of the rooms (FS) remaining spaces a cooling device (K2 - K7) is arranged. Hot strip line according to claim 13, characterized in that the cooling device (K2 - K7) delivers at least one high-pressure water jet, the volume flow of which can be regulated. Hot strip line according to one of claims 13 or 14, characterized in that the cooling device (K2 - K7) comprises a plurality of nozzles which can be supplied with cooling liquid individually or in groups.

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